Temperable coatings comprising diamond-like carbon

ABSTRACT

A coated substrate includes a coating, wherein the coating includes, starting from the substrate in this order: a. a layer of diamond-like carbon, b. a metallic multi-ply layer, wherein the metallic multi-ply layer contains b1) tin and at least one alloying element for tin, or b2) magnesium and at least one alloying element for magnesium, wherein the metallic multi-ply layer is formed from two, three, or more plies, wherein one or more plies contain tin and one or more plies made of at least one alloying element for tin selected from antimony, copper, lead, silver, indium, gallium and/or germanium, are arranged alternatingly, or wherein one or more plies contain magnesium and one or more plies made of at least one alloying element for magnesium selected from aluminum, bismuth, manganese, copper, cadmium, iron, strontium, zirconium, thorium, lithium, nickel, lead, silver, chromium, silicon, tin, gadolinium, yttrium, calcium and/or antimony, are arranged alternatingly.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation of U.S. application Ser. No.16/633,778, filed Jan. 24, 2020, which is the U.S. National Stage ofPCT/EP2018/069617, filed Jul. 19, 2018, which in turn claims priority toEuropean patent application number 17 183 189.4, filed Jul. 26, 2017.The content of these applications are incorporated herein by referencein their entireties.

FIELD

The invention relates to a substrate coated with diamond-like carbon(DLC). More particularly, the invention relates to an improvedmultilayer coating system comprising a DLC layer for providingheat-treatable or temperable DLC layers.

BACKGROUND

For many applications, it is desirable to provide a substrate surfacewith improved scratch resistance. For example, soda lime glass does notinherently have high scratch resistance; however, the application of asuitable thin film can significantly improve the scratch resistance ofthe glass surface.

Thin layers of diamond-like carbon (DLC) are particularly well suitedfor this and their scratch resistance is well known. Extensiveliterature exists for methods for producing DLC coatings.

For example, WO 2004/071981 A2 describes an ion beam method fordepositing DLC layers. CN 105441871 A relates to the production ofsuperhard DLC layers using PVD and HIPIMS methods. CN 104962914 Adescribes an industrial vapor deposition apparatus for depositing DLClayers. Another apparatus for producing DLC layers is described in CN203834012 U. JP 2011068940 A relates to a method for producingabrasion-resistant DLC layers. Furthermore, DE 10 2008 037 871 A1discloses, for example, the use of a DLC layer in a slide bearing.

In many applications, however, it is necessary for the product to beheat treated or tempered. Since DLC is not temperature stable attemperatures above 400° C. and standard tempering processes requiretemperatures to 700° C., the properties of the DLC coatings are degradedthereby or even make them unreasonable since they “burn” the DLC layer.

Two primary methods are known for providing heat-treatable or temperableDLC layers. The first method is based on Si doping of the DLC layersthemselves in order to improve temperature resistance during a heattreatment. In the other method, additional protective and removal layersare used to protect the DLC layer against oxygen (oxygen barrier layers)and thus to prevent the burning of the DLC layer during the heattreatment. The protective and removal layers can be removed again afterthe heat treatment.

Thus, U.S. Pat. No. 7,060,322 B2 describes a coating system, in which aglass coating with a DLC layer is provided a protective layer of,optionally, doped zirconium nitride. The protective layer can be removedagain after a heat treatment.

U.S. Pat. No. 8,580,336 B2 describes a glass coating with a DLC layer,wherein a first and a second inorganic layer are arranged over the DLClayer, wherein the first layer includes zinc oxide and nitrogen. US20080182033 A1 describes a similar coating with a tin oxide layer and anoptional zinc oxide layer.

U.S. Pat. No. 8,443,627 B2 relates to a glass coating with a DLC layer,wherein a release layer and a barrier layer including zinc oxides orzinc suboxides or aluminum nitride are arranged over the DLC layer. Therelease layer preferably includes or is made of oxides, suboxides,nitrides, and/or subnitrides of boron, titanium boride, magnesium, zinc,and mixtures thereof.

The known systems with barrier layers based on substoichiometric zincoxides prevent the oxidation of DLC layers on glass. Release layersbased on magnesium oxides or magnesium suboxides between the DLC layerand the barrier layer facilitated the release after the heat treatment.These layer modifications provide protection for an underlying DLClayer, which is thus temperable. However, the oxygen barrier layers haveto be relatively thick (>100 nm) in order to achieve satisfactoryprotection of the DLC layers. Also, the removal of the barrier layersafter the heat treatment is quite tedious and can, for example, requirewashing with acetic acid solutions. Moreover, release layers based onmagnesium suboxide are hard to handle during the process due to theinstability and reactivity of Mg. In particular, it is difficult tostore the coated glass when the further processing (heat treatment) isnot to be done until later. There can also be problems during productionby sputtering of magnesium in terms of environmental protection, healthprotection, and occupational safety (EHS, environment, health, andsafety).

SUMMARY

The object of the invention is to overcome the above-describeddisadvantages of the prior art. The object consists, in particular, inproviding a protective system for substrates provided with DLC layersthat enables heat treatment or tempering without adversely affecting theDLC layer wherein production, handling, and processing of the coatingsystem before the heat treatment, in particular in terms of EHS, and therelease of the protective system after the heat treatment is simplified.Furthermore, the protective systems should be storage stable and thebarrier layer for oxygen protection should be as thin as possible.

This object is accomplished according to the invention by a coatedsubstrate according to claim 1. The invention also relates, according toanother claim, to a method for producing a heat-treated substrateprovided with a layer of diamond-like carbon. Preferred embodiments ofthe invention are reported in the dependent claims.

The invention thus relates to a coated substrate, wherein the coatingcomprises, in this order, starting from the substrate:

a. a layer of diamond-like carbon (DLC),

b. a metallic, single-ply or multi-ply, layer and

c. an oxygen barrier layer,

wherein the metallic, single-ply or multi-ply, layer b1) includes tin ortin and at least one alloying element for tin, which are presentunalloyed and/or alloyed, in particular as a tin alloy, or b2) magnesiumand at least one alloying element for magnesium, which are presentunalloyed and/or alloyed, in particular as a magnesium alloy.

It was surprisingly found that, with the layer system used according tothe invention, a DLC coating of exceptional quality with high scratchresistance was obtained after the heat treatment, wherein the protectivelayer can be readily removed by simple washing or brushing off withwater. Additionally, the coatings presented good mechanical stabilityand good aging stability before the heat treatment. The EHS situation issignificantly improved, in particular compared to magnesium, especiallyduring removal of the protective layer.

The coated substrate according to the invention thus presents, comparedto coated substrates according to the prior art, improved stability withregard to handling and storability before the heat treatment and anexceptional protective function during the heat treatment. The problemsin terms of EHS during production, storage, handling, and removal of theprotective layer are minimized. Even relatively thin barrier layersprovide good protection. Furthermore, the release of the oxygen barrierlayer with the metallic layer is quickly and easily possible.

BRIEF DESCRIPTION OF THE DRAWINGS

The invention is explained in the following with reference to theattached figures. They depict:

FIG. 1 a general, schematic representation of the structure of thecoated substrates;

FIG. 2 a schematic representation of a coated glass substrate with ametallic, single-ply layer made of magnesium as a reference;

FIG. 3 a schematic representation of a coated glass substrate accordingto the invention with a metallic, single-ply layer made of tin;

FIG. 4 a schematic representation of a coated glass substrate accordingto the invention with a metallic layer containing magnesium and aluminumplies in an alternating arrangement;

FIG. 5 a schematic representation of a coated glass substrate accordingto the invention with a metallic layer, containing magnesium plies andaluminum and/or copper plies in an alternating arrangement;

FIG. 6 a schematic representation of a coated glass substrate accordingto the invention with a metallic, single-ply layer of a magnesium-copperalloy;

DETAILED DESCRIPTION

The substrate of the coated substrate according to the invention can beany substrate. The substrate is preferably made of ceramic, glassceramic, or glass, with the substrate preferably a glass substrate.Preferred examples for glass are soda lime glass, borosilicate glass, oraluminosilicate glass. The soda lime glass can be clear or tinted. In apreferred embodiment, the substrate is a glass pane. The thickness ofthe substrates, in particular of the glass substrates, can vary withinwide ranges, wherein the thickness can, for example, be in the rangefrom 0.1 mm to 20 mm.

The coating of the coated substrate according to the invention includes,starting from the substrate, in this order: a.) a layer of diamond-likecarbon (DLC), b.) a metallic, single-ply or multi-ply, layer, and c.) anoxygen barrier layer. Of the three layers, the layer of diamond-likecarbon is thus situated closest to the substrate. The metallic,single-ply or multi-ply, layer is arranged over the layer ofdiamond-like carbon; and the oxygen barrier layer is arranged over berthe metallic, single-ply or multi-ply, layer.

It should be generally noted that following information concerning thecoated substrate refer to the coated substrate before the heattreatment, unless explicitly indicated otherwise. A heat treatment canresult in changes, in particular with regard to the metallic layer andthe oxygen barrier layer.

Layers made of diamond-like carbon are generally known. Diamond-likecarbon is usually abbreviated to DLC. The layers made of DLC are alsoreferred in the following to as DLC layers. In DLC layers, hydrogen-freeor hydrogen-containing amorphous carbon is the predominant constituent,wherein the carbon can consist of a mixture of sp³ and sp² hybridizedcarbon; optionally, sp³ hybridized carbon or sp² hybridized carbon canpredominate. Examples of DLC are those with the designation ta-C anda:C—H. A DLC layer can can also contain foreign atoms, for example,silicon, metals, oxygen, nitrogen, or fluorine, as doping. The DLC layerused according to the invention can be doped or undoped.

The person skilled in the art knows various methods for producing DLClayers. DLC layers are usually applied on the substrate by a vapordeposition method, e.g., by physical vapor deposition (PVD), e.g., byvapor deposition or sputtering, or by chemical vapor deposition (CVD).Preferably used deposition methods are plasma-enhanced CVD (PECVD) andion beam deposition. In the PECVD method, for example, hydrocarbons, inparticular alkanes and alkynes, such as C₂H₂ or CH₄, can be used asprecursors for the DLC layer to be deposited.

In a particularly preferred embodiment of the invention, the DLC layeris deposited using the so-called magnetron PECVD method, also referredto as the magnetron-enhanced PECVD method. The magnetron PECVD method isa PECVD method, in which the plasma is generated by a magnetron or amagnetron target. The coating of the substrate, which is, optionally,pre-coated with one or more ion diffusion barrier layers, is done in avacuum chamber, in which a magnetron provided with the target and thesubstrate are arranged. At least one reactant gas is introduced into thevacuum chamber under a vacuum, e.g., at a pressure of 0.1 μbar to 10μbar, into the plasma generated by the magnetron target, as a result ofwhich fragments of the reactant gas are formed, that are deposited onthe substrate to form the DLC layer. The reactant gas can, for example,include hydrocarbons, in particular alkanes and alkynes, such as C₂H₂ orCH₄, or organosilicon compounds, e.g., tetramethylsilane. Optionally,additional inert gases, such as argon, can be introduced in the vacuumchamber to enhance the plasma. The magnetron target can, for example, bemade of silicon, which is optionally doped with one or more elements,such as, aluminum and/or boron, or made of titanium. In a particularlypreferred embodiment, the magnetron PECVD method is operated such thatthe magnetron target is in the poisoned mode during the DLC deposition.The operation of such methods in the state of target poisoning is knownto the person skilled in the art and the method parameters can bereadily adjusted accordingly. The production of the DLC layer using themagnetron PECVD method is advantageous since, with it, substrates can becoated with DLC over large areas and with good process stability,without strong heating of the substrate being required. The layers thusproduced have exceptional scratch resistance and good opticalproperties, in particular when the method is operated in the targetpoisoning mode.

In a preferred embodiment, the DLC layer has a layer thickness of 1 nmto 20 nm, preferably of 2 nm to 10 nm, particularly preferably of 3 nmto 8 nm. These layer thicknesses are advantageous since hightransparency of the layers is thus ensured.

The metallic, single-ply or multi-ply, layer contains b1) tin or tin andat least one alloying element for tin, which are present unalloyedand/or alloyed, in particular as a tin alloy, or b2) magnesium and atleast one alloying element for magnesium, which are present unalloyedand/or alloyed, in particular as a magnesium alloy. The alloyingelements for tin or for magnesium are usually metals and/or semimetals.

The metallic, single-ply or multi-ply, layer used according to theinvention has the advantage that it is more stable than prior artlayers. The EHS problems are reduced. Also, this layer is simpler andquicker to remove than prior art layers.

In a particularly preferred embodiment, the metallic, single-ply ormulti-ply, layer contains tin, with the metallic, single-ply ormulti-ply, layer particularly preferably made substantially of tin ormade of tin. In this embodiment, the metallic layer is usuallysingle-ply.

In another embodiment, the metallic, single-ply or multi-ply, layercontains tin and at least one alloying element for tin. Tin and the atleast one alloying element for tin can be present unalloyed and/oralloyed. It is usually advantageous for tin and the at least onealloying element to be present as a tin alloy. This usually simplifiesthe production process. However, it has been found that metallic layers,in which tin and the at least one alloying element for tin are presentnot as a tin alloy, for example, in the form of alternatingly arrangedplies of tin and plies of the at least one alloying element, haveproperties that can be quite similar to a corresponding tin alloy. Sincethe layers are very thin, there are relatively large contact surfacesbetween tin and the at least one alloying element. These are alsoreferred to as so-called “pseudo alloys”.

All customary alloying metals known to the person skilled in the art canbe considered as an alloying element for tin. For example, the at leastone alloying element for tin can be selected from among antimony,copper, lead, silver, indium, gallium, germanium, or a combinationthereof. Particularly preferably, the at least one alloying element fortin is selected from among copper, silver, indium, or a combinationthereof. If the at least one alloying element is selected from among theaforementioned particularly preferred ones, at least one other alloyingelement of the aforementioned not particularly preferred examples can,optionally, be additionally included or not included.

The tin alloy can, for example, be a binary or a ternary alloy. It caneven be a polynary alloy of four or more elements. Accordingly, with thepresence of tin and the at least one alloying element for tin, one, two,three, or more alloying elements for tin can be included.

In another preferred embodiment, the metallic, single-ply or multi-ply,layer contains magnesium and at least one alloying element formagnesium. Magnesium and the at least one alloying element for magnesiumcan be present unalloyed and/or alloyed, in particular as a magnesiumalloy. Usually, it is advantageous for magnesium and the at least onealloying element to be present as a magnesium alloy. This usuallysimplifies the production process. It is in particular advantageous thata magnesium alloy (e.g., with Al and/or Cu) can be used as a target,e.g., for sputtering, since the reactivity of pure magnesium targets isreduced by the alloy, which is advantageous in terms of EHS. This alsoapplies analogously to the coatings produced.

However, it has been found that metallic layers in which magnesium andthe at least one alloying element for magnesium are present in unalloyedform, e.g., in the form of alternatingly arranged layers of magnesiumand of the at least one alloying element have properties that can bequite similar to a corresponding magnesium alloy. Since the layers arevery thin, there are relatively large contact surfaces between magnesiumand the at least one alloying element. These are also referred to asso-called “pseudo alloys”.

All customary alloying metals known to the person skilled in the art canbe considered as an alloying element for magnesium. For example, the atleast one alloying element for magnesium can be selected from amongaluminum, bismuth, manganese, copper, cadmium, iron, strontium,zirconium, thorium, lithium, nickel, lead, silver, chromium, silicon,tin, rare earths, such as, gadolinium or yttrium, calcium, antimony, ora combination thereof. Particularly preferably, the at least onealloying element for magnesium selected from among aluminum, manganese,copper, silicon, or a combination thereof, with aluminum and/or copperparticularly preferable. If the at least one alloying element isselected from among the aforementioned particularly preferred ones, atleast one other alloying element of the aforementioned not particularlypreferred examples can, optionally, be additionally included or notincluded.

Usually, it is preferable that the alloying element for magnesium (if analloying element is used) or at least one alloying element for magnesium(if two or more alloying elements are used) is a metal with a higherstandard electrochemical potential than Mg or a semimetal. Examples of ametal with a higher standard electrochemical potential than Mg are theaforementioned alloying elements aluminum, bismuth, manganese, copper,cadmium, iron, zirconium, nickel, lead, silver, chromium, and tin.Silicon and antimony are examples of semimetals.

The magnesium alloy can, for example, be a binary or ternary alloy. Itcan even be a polynary alloy of four or more elements. Accordingly, withthe presence of magnesium and the at least one alloying element formagnesium, one, two, three, or more alloying elements for magnesium canbe included.

In a preferred embodiment, the metallic, single-ply or multi-ply, layercontains tin, a tin alloy, or a magnesium alloy, in particular tin or amagnesium alloy, with the metallic layer preferably single-ply. Apreferred magnesium alloy contains, as alloying elements, aluminumand/or copper, i.e., a Mg—Al alloy, a Mg—Cu alloy, or a Mg—Al—Cu alloy,wherein one or more additional alloying elements for magnesium can,optionally, be contained in these alloys.

In a preferred embodiment, the metallic layer is formed from two, three,or more plies, wherein one or more plies containing or made of tin andone or more layers containing or made of at least one alloying elementfor tin, preferably selected from copper, silver and/or indium, arearranged alternatingly.

In a particularly preferred embodiment, the metallic layer is formedfrom two, three, or more plies, wherein one or more plies containing ormade of magnesium and one or more plies containing or made of at leastone alloying element for magnesium, preferably selected from aluminumand/or copper, are arranged alternatingly.

Here, “alternating arrangement” means that one or more layers containingtin or with the other variant magnesium (ply a) and one or more pliesincluding at least one alloying element for tin or magnesium (ply b) arearranged alternately, wherein it is irrelevant which ply is appliedfirst; the order of the ply is, consequently, for example: a/b; b/a;a/b/a; b/a/b; a/b/a/b; b/a/b/a/b, etc. The plies containing at least onealloying element for tin or magnesium (ply b) can in each case containthe same alloying element(s); however, different alloying elements canalso be contained in these plies. If two or more alloying elements areincluded, the alloying elements can also be included as an alloy.

For the preferred embodiment magnesium and an alloying element selectedfrom aluminum and/or copper, other exemplary alternating arrangementsare mentioned by way of illustration (see also FIGS. 4 and 5 ): Mg/Al;Mg/Al/Mg; Al/Mg/Al/Mg/Al; Cu/Mg/Cu/Mg/Cu; Al/Mg/Cu/Mg/Al;Al+Cu/Mg/Al+Cu/Mg/Al+Cu.

The metallic layer can be formed from one ply. If the metallic layer isformed from two or more plies, it is possible, for example, for two,three, four, five, or more plies to be included. It is possible, forexample, for up to 40, preferably up to 20 plies to be included. Thethickness of the individual plies can be the same or different. Thethickness a single ply in a multi-ply, metallic layer can, for example,be in the range from 0.5 nm to 20 nm, preferably 1 nm to 12 nm.

In a preferred embodiment, the metallic, single-ply or multi-ply, layerhas, altogether, a layer thickness of 1 nm to 50 nm, preferably of 2 nmto 40 nm, particularly preferably of 4 nm to 25 nm, most preferably 5 nmto 20 nm.

In a preferred embodiment based on tin, the proportion of b1) tin or tinand at least one alloying element for tin in the metallic, single-ply ormulti-ply, layer is, for example, in the range from 90 at.-% to 100at.-%, preferably from 95 at.-% to 100 at.-%, more preferably 98 at.-%to 100 at.-%, particularly preferably 99 at.-% to 100 at.-%, i.e., themetallic layer is made substantially of or is made of tin or tin and atleast one alloying element for tin, with, in the latter case, tin andthe at least one alloying element for tin present unalloyed or alloyed,in particular as a tin alloy.

In a preferred embodiment based on magnesium, the proportion of b2)magnesium and at least one alloying element for magnesium in themetallic, single-ply or multi-ply, layer is, for example, in the rangefrom 90 at.-% to 100 at.-%, preferably from 95 at.-% to 100 at.-%, morepreferably 98 at.-% to 100 at.-%, particularly preferably 99 at.-% to100 at.-%, i.e., the metallic layer is made substantially of or is madeof magnesium and at least one alloying element for magnesium, with, inthe latter case, magnesium and the at least one alloying element formagnesium present unalloyed or alloyed, in particular as a magnesiumalloy.

The metallic layer is preferably made substantially of metals and/ormetal alloys and, optionally, semimetals. Other compounds, such as metaloxides are preferably not included or are included only in smallamounts, for example, as impurities, for example in quantities of lessthan 5 wt.-%, preferably less than 2 wt.-%, and preferably less than 1wt.-%.

In a preferred embodiment based on tin, in which the metallic layer b1)contains tin or tin and at least one alloying element for tin, theproportion of tin in the metallic, single-ply or multi-ply, layer is inthe range from 50 at.-% to 100 at.-%, more preferably from 60 at-% to100 at.-%, even more preferably from 70 at.-% to 100 at.-%, still morepreferably from 70 at.-% to 100 at.-%, still more preferably from 80at.-% to 100 at.-%, and in particular from 90 at.-% to 100 at.-%.

In a preferred embodiment based on magnesium, in which the metalliclayer b1) contains magnesium and at least one alloying element formagnesium, the proportion of magnesium in the metallic, single-ply ormulti-ply, layer is in the range from 50 at.-% to 99 at.-%, morepreferably from 60 at.-% to 95 at.-%.

The metallic, single-ply or multi-ply, layer can be deposited on thesubstrate or the substrate provided with the DLC layer by well-knownmethods or vapor deposition methods, preferably by sputtering,co-sputtering, or ion beam vapor deposition.

Even alloys can be easily sputtered on, for example, with a target ofthe corresponding alloy. The sputtering can also be carried out suchthat deposition onto the substrate is done in an alternating or changingsequence from different targets, by which means even very thin layers(e.g., 1-2 nm thick) of different materials can be applied alternatinglyand a co-mingling of materials is achieved (pseudo alloy). Thealternating sputtering can be achieved, for example, by alternatingpositioning of the substrate and/or of the target. Such an operation isreadily possible with conventional deposition devices.

In co-sputtering, deposition can be done from two or more differenttargets, e.g., two targets of a different metal, at a specific angle ofinclination such that the materials of the different targets co-mingleas homogeneously as possible on the substrate.

The metallic layer serves as a release layer since by means of it, afterthe heat treatment or the tempering, a simple release of the oxygenbarrier layer together with the metallic layer is enabled by a washingprocess.

The coating of the coated substrate according to the invention furtherincludes an oxygen barrier layer. The oxygen barrier layer protects theDLC layer, in particular against ambient oxygen. The oxygen barrierlayer enables subjecting the substrate with the DLC layer situatedthereon to a heat treatment or tempering without causing partial orcomplete degradation of the DLC layer.

Such oxygen barrier layers and their formation are well known in theart. The conventional materials can be used for this.

The usual methods or vapor deposition methods can be used for theapplication of the oxygen barrier layer, for example, PVD, in particularsputtering, preferably magnetron sputtering, CVD, and atomic layerdeposition (ALD).

In a preferred embodiment, the oxygen barrier layer contains a materialselected from silicon carbide, silicon nitride, silicon oxynitride,metal nitride, metal carbide, or a combination thereof or is madesubstantially of such a material, with silicon nitride, metal nitride,metal carbide, or a combination thereof particularly preferred. In thecase of the metal nitrides and metal carbides, the metal can be, forexample, titanium, zirconium, hafnium, vanadium, niobium, tantalum,chromium, molybdenum, or tungsten.

In a particularly preferred embodiment, the oxygen barrier layerincludes or is made substantially of silicon nitride, in particularSi₃N₄ and/or doped Si₃N₄, with Si₃N₄ doped with Zr, Ti, Hf, and/or Bparticularly preferred, and with Zr-doped Si₃N₄ most preferred. With theexception of B, the proportion of the doping elements, in particular ofZr, Ti, and/or Hf in the doped Si₃N₄ can, for example, be in the rangefrom 1 at.-% to 40 at.-%. The proportion of B as a doping element can,for example, be in the range from 0.1 ppm to 100 ppm.

The combination of the metallic layer discussed above with asilver-nitride-containing oxygen barrier layer enables particularly goodprotection of the DLC layer, in particular, when doped Si₃N₄, preferablyZr-doped Si₃N₄, is used for the oxygen barrier layer. This isadvantageous, since, in this way, a relatively thin oxygen barrierlayer, e.g., with a thickness not more than 100 nm or even significantlylower than that, already provides adequate protection. This reducesproduction costs and is also advantageous in terms of simplified releaseof the layers after the heat treatment.

The expression “is made substantially of” used above with reference tothe oxygen barrier layer is understood to mean that said material formsin particular at least 90 wt.-%, preferably at least 95 wt.-%, morepreferably at least 98 wt.-%, of the oxygen barrier layer.

The oxygen barrier layer preferably has a layer thickness of 10 nm to100 nm, preferably of 20 nm to 80 nm, particularly preferably 30 nm to80 nm.

In another preferred embodiment, the proportion of tin and of magnesiumin the oxygen barrier layer is in each case less than 10 at.-%,preferably less than 5 at.-%, and in particular less than 2 at.-%. Thisalso applies for the ranges of tin and magnesium mentioned and/orpreferred in this application.

In another preferred embodiment, for a metallic, single-ply ormulti-ply, layer with a proportion of tin greater than or equal to 50at.-% (and thus also for all ranges mentioned and/or preferred here),the oxygen barrier layer has a proportion of tin or of magnesium of, ineach case, less than 10 at.-%, preferably less than 5 at.-%, and inparticular less than 2 at.-%.

In another preferred embodiment, for a metallic, single-ply ormulti-ply, layer with a proportion of magnesium greater than or equal to50 at.-% (and thus also for all ranges mentioned and/or preferred here),the oxygen barrier layer has a proportion of magnesium or of tin of, ineach case, less than 10 at.-%, preferably less than 5 at.-%, and inparticular less than 2 at.-%.

In an optional and preferred embodiment, the coating further includesone or more ion diffusion barrier layers between the substrate and theDLC layer. The ion diffusion barrier layer prevents, in particular,undesirable diffusion of ions, such as sodium ions, from the substrateinto the coating, in particular during the heat treatment.

Such ion diffusion barrier layers and their formation are well known inthe art. The conventional materials can be used for this. The usualmethods or vapor deposition methods can be used for the application ofion diffusion barrier layers, for example, PVD, in particularsputtering, preferably magnetron sputtering, CVD, or ALD.

In a preferred embodiment, the ion diffusion barrier layer contains amaterial selected from silicon carbide, silicon oxide, silicon nitride,silicon oxynitride, metal oxide, metal nitride, metal carbide, or acombination thereof or is made substantially thereof, with Si₃N₄ and/ordoped Si₃N₄ preferred and with Si₃N₄ doped with Zr, Ti, Hf and/or Bparticularly preferred. In the case of the metal oxides, metal nitrides,and metal carbides, the metal can be, for example, titanium, zirconium,hafnium, vanadium, niobium, tantalum, chromium, molybdenum, or tungsten.

The expression “is made substantially of” used above with reference tothe ion diffusion barrier layer is understood to mean that said materialforms in particular at least 90 wt.-%, preferably at least 95 wt.-%,more preferably at least 98 wt.-%, der ion diffusion barrier layer.

The ion diffusion barrier layer has, for example, a layer thickness of 1nm to 100 nm, preferably of 5 nm to 50 nm.

A particularly preferred embodiment is a coated substrate in which themetallic, single-ply or multi-ply, layer contains tin or is a tin layer,the oxygen barrier layer contains or is made substantially of Si₃N₄and/or doped Si₃N₄, in particular Si₃N₄ doped with Zr, and, optionally,at least one ion diffusion barrier layer is arranged between thesubstrate and the DLC layer, which ion diffusion barrier layer containsor is made substantially of Si₃N₄ and/or doped Si₃N₄, in particularSi₃N₄ doped with Zr.

Another preferred embodiment corresponds to that mentioned above exceptthat instead of tin, the metallic, single-ply or multi-ply, layercontains or is made substantially of a magnesium alloy, in particular amagnesium alloy with Al and/or copper. Alternatively, the metallic,single-ply or multi-ply, layer can contain, instead of the magnesiumalloy, magnesium and at least one alloying element for magnesium, inparticular Al and/or copper, in unalloyed form, in particular not as amagnesium alloy.

In another advantageous embodiment, the substrate, and in particular theglass substrate, together with the layer of diamond-like carbon and oneor more optional ion diffusion barrier layers is transparent, in otherwords, the visible-light transmittance is more than 50%, preferably morethan 70%, and in particular more than 80%.

The invention further relates to a method for producing a heat-treatedsubstrate with a coating including a layer of diamond-like carbon,comprising:

a. heat treatment of a coated substrate according to the invention asdescribed above, and

b. removing the oxygen barrier layer and the metallic, single-ply ormulti-ply, layer from the heat-treated, coated substrate by a washingprocess.

The heat treatment can be tempering. The heat treatment or thetempering, for example, for a glass substrate, can be carried out, forexample, at a temperature of 300° C. to 800° C., preferably 500° C. to700° C., more preferably 600° C. to 700° C. The duration of the heattreatment varies depending on the system treated and the temperatureused but can be, for example, 1 min to 10 min.

For the washing process, water, acids, bases, and organic solvents, forexample, can be used as a washing medium, with water preferred. Thewashing process can be done, for example, by rinsing with the washingmedium, by washing under the action of brushes, or preferably by dippinginto the washing medium. The washing process can be carried out atambient temperature (e.g., in the range from 15° C. to 30° C.). Thewashing medium can optionally also be heated. Usually, the oxygenbarrier layer and the metallic layer can be removed with no problem bysimple dipping into a water bath.

The method according to the invention is suitable for efficient and safeproduction of a heat-treated substrate provided with a DLC layer. Due tothe relatively nonreactive metallic layer, the risk to the product, theequipment, and the worker is reduced. Furthermore, the metallic layerand the oxygen barrier layer can be released quickly and easily.

The invention is further explained in the following with reference tononrestrictive exemplary embodiments and the accompanying drawings. Thefigures are schematic drawings; proportions are not taken into account.

FIG. 1 depicts schematically a structure of coated substrates accordingto the invention. The substrate 1 can, for example, be glass, glassceramic, or ceramic, with glass being preferred, in particular a glasspane. An optional ion diffusion barrier layer 5 is applied on thesubstrate 1. The ion diffusion barrier layer 5 is, for example, formedfrom silicon nitride, preferably doped silicon nitride. A DLC layer 2 issituated on the ion diffusion barrier layer 5. A metallic layer 3 issituated on the DLC layer 2. The metallic layer 3 can be constructedwith a single ply or multiple plies (not shown). It can, for example, bea layer made of tin or of a magnesium alloy, for example, Mg/Cu orMg/Al. Alternatively, the metallic layer 3 can be made of magnesium andat least one alloying element for Mg, e.g., Al and/or Cu. An oxygenbarrier layer 4 is placed on the metallic, single-ply or multi-ply,layer 3. The oxygen barrier layer 4 is formed, for example, from siliconnitride, preferably doped silicon nitride.

This coating system can be heat treated or tempered even at hightemperatures, without adversely affecting the quality of the DLC layer.After the heat treatment, the no longer needed oxygen barrier layer 4and the metallic layer 3 can be released in a simple manner, e.g., bydipping into a water bath.

EXAMPLES

Four coated substrates were produced in laboratory scale. The layerstructure of Example 1 is reported in FIG. 2 . The layer structure ofExample 2 is reported in FIG. 3 . The layer structure of Example 3 isreported in FIG. 4 . The layer structure of Example 4 is reported inFIG. 5 .

Example 1 is a reference example. The Examples 2 to 4 are examplesaccording to the invention.

In all examples, the DLC layer was applied in each case by a PECVDmethod (e.g., with C₂H₂ as a precursor for DLC). The other layers wereapplied on the substrate by a PVD method (magnetron sputtering),wherein, for this, the process parameters indicated in the followingwere used in each case for the individual layers. Alternating plies ofdifferent materials were obtained by alternating with different targets.

Layer Power Pressure Ar flow N₂ Flow Si₃N₄ 7.5 kW 3 μbar 300 sccm 170sccm Mg 3.5 kW 3 μbar 300 sccm — Al 2.0 kW 3 μbar 300 sccm — Cu 2.0 kW 3μbar 300 sccm — Sn 2.0 kW 3 μbar 300 sccm —

Example 1 (Reference)

The structure of the coating produced in Example 1 is depictedschematically in FIG. 2 . The substrate (“Glas”) is a soda lime glasswith a thickness of approx. 2.1 mm. Here, as an alternative, as also inthe following Examples 2 to 4, a soda lime glass with a thickness ofapprox. 3.9 mm was also investigated. An ion diffusion barrier layer(“Si₃N₄”) of Si₃N₄ is applied on the glass substrate. The thickness ofthe ion diffusion barrier layer is 20 nm. Situated above it is a layerof diamond-like carbon (“DLC”) with a thickness of 3 nm to 8 nm. This isfollowed by a metallic layer of magnesium (“Mg”) with a thickness of 10nm. The oxygen barrier layer (“Si₃N₄”) is formed on the magnesium layer.It is made of Si₃N₄ and has a thickness of 50 nm.

Example 2

The structure of the coating produced in Example 2 is depictedschematically in FIG. 3 . The substrate (“Glas”) is a soda lime glasswith a thickness of approx. 2.1 mm. An ion diffusion barrier layer(“Si₃N₄”) of Si₃N₄ is applied on the glass substrate. The thickness ofthe ion diffusion barrier layer is 20 nm. Situated above it is a layerof diamond-like carbon (“DLC”) with a thickness of 3 nm to 8 nm. This isfollowed by a metallic layer made of tin (“Sn”) with a thickness of 10nm. The oxygen barrier layer (“Si₃N₄”) is formed on the tin layer. It ismade of Si₃N₄ and has a thickness of 50 nm.

Example 3

The structure of the coating produced in Example 3 is depictedschematically in FIG. 4 . The substrate (“Glas”) is a soda lime glasswith a thickness of approx. 2.1 mm. An ion diffusion barrier layer(“Si₃N₄”) of Si₃N₄ is applied on the glass substrate. The thickness ofthe ion diffusion barrier layer is 20 nm. Situated above it is a layerof diamond-like carbon (“DLC”) with a thickness of 3 nm to 8 nm. This isfollowed by a three-ply metallic layer, formed alternatingly bymagnesium and aluminum. The metallic layer starts with a 2-nm-thick ply(“Al”) of aluminum, followed by a 10-nm-thick ply (“Mg”) of magnesium,followed by another 2-nm-thick ply (“Al”) of aluminum. Situated abovethis is an oxygen barrier layer (“Si₃N₄”), which is made of Si₃N₄ andhas a thickness of 50 nm.

Example 4

The structure of the coating produced in Example 4 is depictedschematically in FIG. 5 . The substrate (“Glas”) is a soda lime glasswith a thickness of approx. 2.1 mm. An ion diffusion barrier layer(“Si₃N₄”) of Si₃N₄ is applied on the glass substrate. The thickness ofthe ion diffusion barrier layer is 20 nm. Situated above it is a layerof diamond-like carbon (“DLC”) with a thickness of 3 nm to 8 nm. Twovariants were tested for the metallic layer. In one variant, Mg and Alwere used; and in the other variant, Mg and Cu. From this, a multi-plymetallic layer was formed, respectively alternating magnesium andaluminum or alternating magnesium and copper. The metallic layer startswith a ply (“Mg”) of magnesium, followed by a ply (“Al/Cu”) of aluminumor copper, followed by a ply (“Mg”) of magnesium, etc. In FIG. 5 , notall plies applied are depicted, which is symbolized by “ . . . ”. Themetallic layer ends with a ply of magnesium (not shown). All plies ofthe metallic layer have a thickness of approx. 2 nm. The total thicknessof the metallic layer is approx. 20 nm. The result is that the metalliclayer consists of approx. 10 alternating plies. Situated above themetallic ply is an oxygen barrier layer (“Si₃N₄”), which is made ofSi₃N₄ and has a thickness of 50 nm.

Alternatively, it would be conceivable to form a metallic layer from Mg,Al and Cu. For this, for example, an alternating layer sequenceMg/Al/Mg/Cu/Mg/Al, etc., could be selected. In another variant, Cu andAl could be applied together, e.g., as an alloy, which would yield, forexample, the following layer sequence: Mg/Cu+Al/Mg/Cu+Al, etc.

Evaluation of Examples 1 to 4

The coatings of all examples presented good temperability andexceptionally good scratch resistance after heat treatment and removalof the metallic layer and the oxygen barrier layer. The DLC layer wasthus successfully protected by the oxygen barrier layer of Si₃N₄ againstdegradation and oxidation in all examples.

In particular, oxygen barrier layers of Si₃N₄ that were doped with Zrpresented excellent protection for the DLC layer during tempering.

After a heat treatment, the metallic layers of Examples 2, 3, and 4 (Snor Mg and Al or Cu) proved to be advantageous as fracture or releasepoints. AH that was needed to remove layers situated above the DLC layerwas a treatment with water.

Also, the metallic layers of Examples 2, 3, and 4 (Sn or Mg and Al orCu) presented good mechanical stability before tempering, facilitatingprocessing and storage of the not yet heat-treated glass.

The following table presents the relative behavior of the coatedsubstrates of Examples 1 to 4 in terms of storage stability, EHS risk,and scratch resistance (“−”=unsatisfactory, “o” adequate; “+”=good)

Example 1 Example 2 Example 3 Example 4 Storage Stability − + + ∘ EHSRisk − + ∘ ∘ Scratch Resistance + + + +

Storage Stability Test

The coated glass substrates of Examples 1 to 4 were stored for eightweeks after production (without tempering) under atmospheric conditionsand examined for signs of aging.

Example 1 presented poor layer adhesion and corrosion; the coating couldbe removed by mere rubbing with a finger. Example 4 occasionallypresented areas in which similar adhesion problems occurred. ForExamples 2 and 3, none of these weaknesses could be detected.

In Example 1, the degrading effect of moisture during storage is clearlyshown. Whereas shortly after production of the coating, Example 1presented good behavior similar to that of Example 2 in terms ofadhesion and protection, after 2 months of storage, there was ablationof the coating, as a result of which the DLC layer is partially exposed.In this condition, a heat treatment is no longer possible since there isno longer adequate protection for the DLC layer. Coatings according toExample 1 are, consequently, only usable when the heat treatment iscarried out shortly after production of the coating. In contrast, withthe coating of Example 2, no release of the coating is discernible evenafter 2 months and it offers very much better storage and handlingproperties.

EHS Risk

EHS risk includes an evaluation of the EHS risk situation for theproduction and handling of the coated substrates. Since metallicmagnesium has a certain reactivity, this must always be taken intoaccount, in particular in the sputtering process, where fine dustsdevelop (Example 1). As a result of the combination with less reactivematerials (Al/Cu), the risk is reduced (Examples 3 and 4). This risk issubstantially eliminated in Example 2, since Sn is significantly lessreactive than Mg.

Scratch Resistance

The DLC-coated substrates obtained from Examples 1 to 4 after thetempering process and after removal of the metallic layer presented,compared to non-coated soda lime glass, good resistance to scratching ina test with increasing exposure.

For this, stainless-steel, borosilicate, and aluminum oxide spheres witha 10-mm diameter were made to act with increasing force (uniformincrease in force from 0 N to 30 N by increasing the drop height, speed30 N/min) on the coated substrates and, for comparison, on uncoated sodalime glass. The stainless-steel spheres left no scratch marks on anyspecimen. Already starting from a force of approx. 5 N, the borosilicateand aluminum oxide spheres left deep marks on the uncoated soda limeglass but no marks on the coated glass.

Also, the coefficient of friction of the DLC coated substrates obtainedfrom Examples 1 to 4 was compared with the coefficient of friction ofuncoated soda lime glass: The coefficient of friction for Examples 1 to4 was comparable and significantly lower than that for uncoated sodalime glass. Similar results were found with coated and non-coatedborosilicate glass and coated and non-coated stainless steel. Thecoefficient of friction is significantly reduced by the coating.

FIG. 6 illustrates another embodiment of a coated substrate according tothe invention. The substrate (“Glas”) is a glass substrate. An iondiffusion barrier (“Si₃N₄”) of Si₃N₄ is applied on the glass substrate.A DLC layer (“DLC”) is situated above it. This is followed by a metalliclayer (“Mg+Cu”) of a Mg—Cu alloy. Alternatively, a Mg—Al or a Mg—Al—Cualloy, for example, would be conceivable. An oxygen barrier layer(“Si₃N₄”) is situated on the metallic layer.

LIST OF REFERENCE CHARACTERS

-   1 substrate-   2 layer of diamond-like carbon (DLC)-   3 metallic, single-ply or multi-ply, layer-   4 oxygen barrier layer-   5 ion diffusion barrier layer (optional)

The invention claimed is:
 1. A coated substrate comprising a coating,wherein the coating comprises, starting from the substrate in thisorder: a. a layer of diamond-like carbon, b. a metallic multi-ply layer,wherein the metallic multi-ply layer contains b1) tin and at least onealloying element for tin, or b2) magnesium and at least one alloyingelement for magnesium, wherein the metallic multi-ply layer is formedfrom two, three, or more plies, wherein one or more plies contain tinand one or more plies made of at least one alloying element for tinselected from antimony, copper, lead, silver, indium, gallium and/orgermanium, are arranged alternatingly, or wherein one or more pliescontain magnesium and one or more plies made of at least one alloyingelement for magnesium selected from aluminum, bismuth, manganese,copper, cadmium, iron, strontium, zirconium, thorium, lithium, nickel,lead, silver, chromium, silicon, tin, gadolinium, yttrium, calciumand/or antimony, are arranged alternatingly.
 2. The coated substrateaccording to claim 1, wherein the coating further comprises, between thesubstrate and the layer of diamond-like carbon, one or more iondiffusion barrier layers, which contain or are made of silicon carbide,silicon oxide, silicon nitride, silicon oxynitride, metal oxide, metalnitride, metal carbide, or a combination thereof.
 3. The coatedsubstrate according to claim 1, wherein the layer of diamond-like carbonhas a layer thickness of 1 nm to 20 nm, and/or the metallic multi-plylayer has a layer thickness of 1 nm to 50 nm.
 4. The coated substrateaccording to claim 3, wherein the layer of diamond-like carbon has alayer thickness of 2 nm to 10 nm, and/or the metallic multi-ply layerhas a layer thickness of 5 nm to 25 nm.
 5. The coated substrateaccording to claim 1, wherein the substrate is ceramic, glass ceramic,or glass.
 6. The coated substrate according to claim 1, wherein themetallic multi-ply layer is formed by sputtering, or by CVD, or by ionbeam vapor deposition.
 7. The coated substrate according to claim 1,wherein the layer of diamond-like carbon is undoped or doped.
 8. Thecoated substrate according to claim 1, wherein the coating furthercomprises an oxygen barrier layer that is directly formed on themetallic multi-ply layer.
 9. The coated substrate according to claim 8,wherein the proportion of tin or of magnesium in the oxygen barrierlayer is <10 at.-%.
 10. The coated substrate according to claim 9,wherein the proportion of tin or of magnesium in the oxygen barrierlayer is <2 at.-%.
 11. The coated substrate according to claim 8,wherein the oxygen barrier layer contains or is made of silicon carbide,silicon nitride, silicon oxynitride, metal nitride, metal carbide, or acombination thereof.
 12. The coated substrate according to claim 8,wherein the oxygen barrier layer has a layer thickness of 10 to 100 nm.13. A method for producing a heat-treated substrate with a coatingcomprising a layer of diamond-like carbon, comprising: a. heat-treatinga coated substrate according to claim 9, at a temperature of 300 to 800°C., and b. removing the oxygen barrier layer and the metallic multi-plylayer from the heat-treated, coated substrate by a washing process. 14.The coated substrate according to claim 1, wherein the one or more pliescontaining tin are made of tin, or the one or more plies containingmagnesium are made of magnesium.
 15. The coated substrate according toclaim 1, wherein the one or more plies containing tin contain alloyedtin, wherein tin is alloyed with at least one alloying element for tinselected from antimony, copper, lead, silver, indium, gallium and/orgermanium, or the one or more plies containing magnesium contain alloyedmagnesium, wherein magnesium is alloyed with at least one alloyingelement for magnesium selected from aluminum, bismuth, manganese,copper, cadmium, iron, strontium, zirconium, thorium, lithium, nickel,lead, silver, chromium, silicon, tin, gadolinium, yttrium, calciumand/or antimony.
 16. A coated substrate comprising a coating, whereinthe coating comprises, starting from the substrate in this order: a. alayer of diamond-like carbon, b. a metallic, single-ply or multi-ply,layer, wherein the metallic, single-ply or multi-ply, layer contains tinor tin and at least one alloying element for tin, which are presentunalloyed and/or alloyed, and the proportion of tin in the metallic,single-ply or multi-ply, layer is in the range from 50 at.-% to 100at.-%.
 17. The coated substrate according to claim 16, wherein thecoating further comprises an oxygen barrier layer that is directlyformed on the metallic multi-ply layer.